EP2546375B1 - High-strength pressed member and method for producing same - Google Patents

High-strength pressed member and method for producing same Download PDF

Info

Publication number
EP2546375B1
EP2546375B1 EP11752999.0A EP11752999A EP2546375B1 EP 2546375 B1 EP2546375 B1 EP 2546375B1 EP 11752999 A EP11752999 A EP 11752999A EP 2546375 B1 EP2546375 B1 EP 2546375B1
Authority
EP
European Patent Office
Prior art keywords
inclusive
steel sheet
steel
seconds
temperature
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP11752999.0A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP2546375A1 (en
EP2546375A4 (en
Inventor
Hiroshi Matsuda
Yoshimasa Funakawa
Yasushi Tanaka
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=44563169&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP2546375(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP2546375A1 publication Critical patent/EP2546375A1/en
Publication of EP2546375A4 publication Critical patent/EP2546375A4/en
Application granted granted Critical
Publication of EP2546375B1 publication Critical patent/EP2546375B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a high strength press-formed member mainly for use in the field of automobile industry, in particular, a high strength press-formed member having tensile strength (TS) of at least 980 MPa and prepared by hot press-forming a heated steel sheet within a mold constituted of a die and a punch.
  • TS tensile strength
  • the present invention also relates to a method for manufacturing the high strength press-formed member.
  • GBP 1490535 discloses what is called “hot/warm press forming” as a method for manufacturing a member by press-forming a heated steel sheet in a mold and then immediately and rapidly cooling the steel sheet to increase strength thereof.
  • the method has already been applied to manufacturing some members requiring TS in the range of 980 MPa to 1470 MPa.
  • This method characteristically alleviates the aforementioned formability deterioration problem, as compared with what is called “cold press-forming” at the room temperature, and can highly increase strength of a subject member by utilizing low-temperature transformed microstructure obtained by water-quenching.
  • JP-A 2007-016296 a hot press-formed member manufactured by hot press-forming a steel sheet at temperature in the two-phase region of (ferrite + austenite) such that the steel sheet has: dual-phase microstructure constituted of40%-90% ferrite and 10%-60% martensite by 5 area ratio after the hot press-forming; TS in the range of 780 MPa to 1180 MPa class; and excellent ductility of total elongation in the range of 10% to 20%.
  • a generic steel sheet is for instance known from US 2008/0000555 A1 .
  • Patent Document discloses a high strength thin-gauge steel sheet with excellent elongation and hole expandability having a tensile strength of 500 MPa or more and a method of production of high strength thin-gauge steel sheet with excellent elongation and hole expandability enabling production of this on an industrial scale.
  • the high strength thin-gauge steel sheet of US 2008/0000555 A1 comprises , by mass % C: 0.03 to 0.25%, Si: 0.4 to 2.0%, Mn: 0.8 to 3.1%, P ⁇ 0.02%, S ⁇ 0.02%, Al ⁇ 2.0%, N ⁇ 0.01%, and a balance of Fe and unavoidable impurities, which has a microstructure comprised of ferrite with an area fraction of 10 to 85% and residcual austenite with a volume fraction of 1 to 10%, an area fraction of 10% to 60% of the tempered martensite, and a balance of bainite.
  • the hot press-formed member disclosed in JP-A 2007-016296 does not reliably exhibit sufficient ductility, although the member has tensile strength around 1270 MPa. Therefore, it is still necessary to develop a member having high strength and excellent ductility in a compatible manner in order to achieve further reduction of automobile body weight.
  • the present invention aims at advantageously solving the aforementioned problems and an object thereof is to provide a high strength press-formed member having tensile strength of at least 980 MPa and excellent ductility of (TS x T. EL.) > 17000 (MPa ⁇ %), as well as an advantageous manufacturing method of the high strength press-formed member.
  • the inventors of the present invention as a result of a keen study of component composition and microstructure of a steel sheet to solve the aforementioned problems, discovered that it is possible to obtain a high strength press-formed member excellent in strength and ductility and having tensile strength of at least 980 MPa by: highly increasing strength of a steel sheet by utilizing martensite microstructure; ensuring retained austenite, which is advantageous in terms of obtaining a TRIP (Transformation Induced Plasticity) effect, in a stable manner by increasing carbon content in the steel sheet to a relatively high level, i.e. at least 0.12 mass %, and utilizing bainitic transformation; and tempering a portion of martensite.
  • TRIP Transformation Induced Plasticity
  • tempered state of martensite and a state of retained austenite were studied in detail.
  • tempered martensite, retained austenite and bainitic ferrite are adequately made into a composite material and thus a high strength hot press-formed member having high strength and excellent ductility can be manufactured by cooling a steel sheet before retained austenite is rendered stable due to bainitic transformation, to allow a portion of martesite to be formed.
  • the present invention provides a high strength press-formed member obtainable by hot-press forming as defined in claim 1. According to a further aspect, the invention provides a method for manufacturing high strength press-formed member as defined in claim 2.
  • TS tensile strength
  • FIG. 1 is a diagram showing a temperature range of hot press forming in a method for manufacturing a press-formed member according to the present invention.
  • Area ratio of a phase represents area ratio of the phase with respect to the entire microstructure of a steel sheet hereinafter.
  • Area ratio of martensite 10% to 85% (inclusive of 10% and 85%) Martensite, which is a hard phase, is a microstructure necessitated for increasing strength of a steel sheet.
  • Tensile strength (TS) of a steel sheet fails to reach 980 MPa when area ratio of martensite is less than 10%.
  • Area ratio of martensite exceeding 85% results in insufficient content of bainite and failure in reliably obtaining sufficient content of retrained austenite having relatively high carbon concentration therein in a stable state, thereby causing a problem of deteriorated ductility.
  • area ratio of martensite is to be in the range of 10% to 85% (inclusive of 10% and 85%), preferably in the range of 15% to 80% (inclusive of 15% and 80%), more preferably in the range of 15% to 75% (inclusive of 15% and 75%), and particularly preferably in the range of 15% to 70% (inclusive of 15% and 70%).
  • a steel sheet may have poor toughness to cause brittle fracture during press-forming, although the steel sheet has tensile strength of at least 980 MPa, in a case where proportion of tempered martensite with respect to the whole martensite present in the steel sheet is less than 25%. Martensite which has been quenched but not tempered yet is very hard and poor in deformability. However, deformability of such brittle martensite as described above remarkably improves by itself by tempering of the steel sheet, so that ductility and toughness of the steel sheet improve. Therefore, proportion of tempered martensite with respect to the whole martensite present in a steel sheet is to be at least 25% and preferably at least 35%.
  • Tempered martensite is visually observed by using a scanning electron microscope (SEM) or the like as martensite microstructure having fine carbides precipitated therein, which microstructure can be clearly differentiated from quenched but not tempered martensite having no such carbides therein.
  • SEM scanning electron microscope
  • Retained austenite experiences martensitic transformation due to a TRIP effect when a steel sheet is processed, thereby contributing to improvement of ductility of the steel sheet through enhanced strain-dispersibility thereof.
  • Retained austenite having in particular enhanced carbon concentration therein is formed in bainite by utilizing bainitic transformation in the steel sheet of the present invention.
  • the steel sheet of the present invention can exhibit good formability in a high strength region having tensile strength (TS) of at least 980 MPa, specifically has a value of (TS ⁇ T. EL.) ⁇ 17000 (MPa ⁇ %) and thus attains good balance between high strength and excellent ductility by allowing retained austenite and martensite to coexist and utilizing these two types of microstructures.
  • Retained austenite in bainite is formed and finely distributed between laths of bainitic ferrite in bainite, whereby lots of measurements at relatively high magnification are necessary to determine content (area ratio) thereof through visual observation of the microstructures. In short, it is difficult to accurately carry out quantitative analysis of retained austenite. On the other hand, it has been confirmed that content of retained austenite formed between laths ofbainitic ferrite has reasonable correlation with content of bainitic ferrite thus formed.
  • XRD X-ray diffraction
  • content of retained austenite is to be in the range of 5% to 40% (inclusive of 5% and 40%), preferably in the range of 5% to 40% (exclusive of 5% and inclusive of 40%), more preferably in the range of 10% to 35% (inclusive of 10% and 35%), and further more preferably in the range of 10% to 30% (inclusive of 10% and 30%).
  • the average carbon concentration in retained austenite is important in terms of obtaining excellent formability by utilizing a TRIP effect in a high strength steel sheet having tensile strength (TS) in the range of 980 MPa to 2.5 GPa class. Carbon concentration in retained austenite formed between laths of bainitic ferrite in bainite is enhanced in the steel sheet of the present invention. It is difficult to accurately determine content of carbon concentrated in retained austenite between laths of bainitic ferrite in bainite.
  • the inventors of the present invention found out that satisfactorily excellent formability of a steel sheet can be obtained when the average carbon concentration in retained austenite (the average of carbon concentration distributed within retained austenite), determined from a magnitude of shift of a diffraction peak in X-ray diffraction (XRD) according to the conventional method for measuring the average carbon concentration in retained austenite, is at least 0.65%.
  • XRD X-ray diffraction
  • the average carbon concentration in retained austenite lower than 0.65% may cause martensitic transformation to occur in a low strain region in processing of a steel sheet, which results in insufficient TRIP effect in a high strain region (the TRIP effect in a high strain region effectively improves formability of a steel sheet). Accordingly, the average carbon concentration in retained austenite is to be at least 0.65% and preferably at least 0.90%.
  • the average carbon concentration in retained austenite exceeding 2.00% renders retained austenite too stable, whereby martensitic transformation does not occur during processing of a steel sheet, a TRIP effect fails to be expressed and thus ductility of the steel sheet may deteriorate. Accordingly, the average carbon concentration in retained austenite is preferably 2.00% or less and more preferably 1.50% or less.
  • Transformation from austenite into bainite occurs over a wide temperature range from 150°C to 550°C and various types of bainite are formed within this temperature range.
  • the target bainite microstructure is preferably specified in terms of reliably attaining desired formability in the present invention, although such various types of bainite as described above were simply and collectively referred to as "bainite" in the prior art in general.
  • these two types of bainite are defined as follows.
  • Upper bainite is constituted of lath-like bainitic ferrite, and retained austenite and/or carbide existing between laths of bainitic ferrite and characterized in that it lacks fine carbides regularly aligned between the laths of bainitic ferrite.
  • lower bainite constituted of lath-like bainitic ferrite and retained austenite and/or carbide existing between laths of bainitic ferrite as in upper bainite, does characteristically include fine carbides regularly aligned between the laths of bainitic ferrite. That is, upper bainite and lower bainite are differentiated by presence/absence of fine carbides regularly aligned in bainitic ferrite.
  • Upper bainite is more preferable than lower bainite as bainite to be formed in the present invention.
  • bainite thus formed is lower bainite or mixture of upper bainite and lower bainite.
  • Area ratio of bainite with respect to the entire microstructure of a steel sheet is preferably in the range of 20% to 75%.
  • the total of area ratios of martensite, retained austenite, and bainitic ferrite in bainite at least 65%
  • the area ratios of martensite, retained austenite, and bainitic ferrite in bainite individually satisfying the respective preferable ranges thereof described above do not suffice and it is necessary that the total of area ratios of martensite, retained austenite, and bainitic ferrite in bainite with respect to the entire microstructure of the steel sheet is at least 65%.
  • the total of area ratios described above lower than 65% may result in at least one of insufficient strength and poor formability of a resulting steel sheet.
  • the aforementioned total of area ratios is preferably at least 70% and more preferably at least 75%.
  • the steel sheet of the present invention may include polygonal ferrite, pearlite and widmanstatten ferrite as remaining microstructures.
  • the acceptable content of such remaining microstructures as described above is preferably 30% or less and more preferably 20% or less by area ratio with respect to the entire microstructure of the steel sheet.
  • C 0.12% to 0.69% (inclusive of 0.12% and 0.69%) Carbon is an essential element in terms of increasing strength of a steel sheet and reliably obtaining required content of stable retained austenite. Further, carbon is an element required for ensuring necessitated content of martensite and making austenite be retained at the room temperature. Carbon content in steel lower than 0.12% makes it difficult to ensure high strength and good formability of a steel sheet. Carbon content exceeding 0.69% significantly hardens a welded portion and surrounding portions affected by welding heat, thereby deteriorating weldability of a steel sheet.
  • carbon content in steel is to be in the range of 0.12% to 0.69% (inclusive of 0.12% and 0.69%), preferably in the range of 0.20% to 0.48% (exclusive of 0.20% and inclusive of 0.48%), and more preferably in the range of 0.25% to 0.48% (inclusive of 0.25% and 0.48%).
  • Silicon is a useful element which contributes to increasing strength of a steel sheet through solute strengthening.
  • silicon content in steel exceeding 3.0% deteriorates: formability and toughness due to increase in content of solute Si in polygonal ferrite and bainitic ferrite; surface quality of the steel sheet due to generation of red scales or the like; and coatability and coating adhesion of plating when the steel sheet is subjected to hot dip galvanizing.
  • Si content in steel is to be 3.0% or less, preferably 2.6% or less, and more preferably 2.2% or less.
  • Silicon content in steel is preferably at least 0.5% because silicon is a useful element in terms of suppressing formation of carbide and facilitating formation of retained austenite.
  • silicon need not be added and thus Si content may be zero % in a case where formation of carbide is suppressed solely by aluminum.
  • Mn 0.5% to 3.0% (inclusive of 0.5% and 3.0%)
  • Manganese is an element which effectively increases steel strength.
  • Manganese content less than 0.5% in steel causes carbide to be precipitated at temperature higher than the temperature at which bainite and martensite are formed when a steel sheet is cooled after annealing, thereby making it impossible to reliably obtain a sufficient content of hard phase contributing to steel strengthening.
  • Mn content exceeding 3.0% may deteriorate forgeability of steel. Accordingly, Mn content in steel is to be in the range of 0.5% to 3.0% (inclusive of 0.5% and 3.0%) and is preferably in the range of 1.0% to 2.5% (inclusive of 1.0% and 2.5%).
  • Phosphorus is a useful element in terms of increasing steel strength.
  • phosphorus content in steel exceeding 0.1 % makes steel brittle due to grain boundary segregation of phosphorus to deteriorate impact resistance of a resulting steel sheet; and significantly slows galvannealing (alloying) rate down in a case the steel sheet is subjected to galvannealing.
  • phosphorus content in steel is to be 0.1 % or less and preferably 0.05% or less.
  • the lower limit of phosphorus content in steel is preferably around 0.005% because an attempt to reduce the phosphorus content below 0.005% would significantly increase production cost, although phosphorus content in steel is to be decreased as best as possible.
  • Aluminum is a useful element added as a deoxidizing agent in a steel manufacturing process.
  • aluminum content exceeding 3.0% may deteriorate ductility of a steel sheet due to too much inclusion in the steel sheet.
  • aluminum content in steel is to be 3.0% or less and preferably 2.0% or less.
  • aluminum is a useful element in terms of suppressing formation of carbide and facilitating formation of retained austenite.
  • Aluminum content in steel is preferably at least 0.001% and preferably at least 0,005% to sufficiently obtain a good deoxidizing effect of aluminum.
  • Aluminum content in the present invention represents content of aluminum contained in a steel sheet after deoxidization.
  • Nitrogen is an element which most significantly deteriorates anti-aging property of steel and thus content thereof in steel is preferably decreased as best as possible. Nitrogen content in steel exceeding 0.010% makes deterioration of anti-aging property of steel apparent. Accordingly, nitrogen content in steel is to be 0.010% or less. The lower limit of nitrogen content in steel is around 0.001% in view of production cost because decreasing nitrogen content in steel below 0.001% would significantly increase production cost.
  • Silicon and aluminum are useful elements, respectively, in terms of suppressing formation of carbides and facilitating formation of retained austenite. Such good effects of suppressing carbide formation caused by Si and Al as described above are each independently demonstrated when only one of Si and Al is included in steel. However, these carbide formation-suppressing effects of Si and Al improve when the total content of Si and Al is at least 0.7% in the present invention.
  • composition of the steel sheet of the present invention may further include, in addition to the aforementioned basic components, following components in an appropriate manner.
  • Cr 0.05% to 5.0%
  • V 0.005% to 1.0%
  • Mo 0.005% to 0.5%
  • Chromium, vanadium and molybdenum are elements which each suppress formation of pearlite when a steel sheet is cooled from the annealing temperature.
  • Titanium and niobium are useful elements in terms of precipitate strengthening/hardening of steel. Titanium and niobium can each cause this effect when contents thereof in steel are at least 0.01 %, respectively. In a case where at least one of Ti content and Nb content in steel exceeds 0.1%, formability and shape fixability of a resulting steel sheet deteriorate. Accordingly, in a case where the steel sheet composition includes Ti and Nb, contents thereof are to be Ti: 0.01% to 0.1% (inclusive of 0.01% and 0.1 %), and Nb: 0.01% to 0.1 % (inclusive of 0.01% and 0.1 %), respectively.
  • Boron is a useful element in terms of suppressing formation and growth of polygonal ferrite from austenite grain boundary. This good effect of boron can be obtained when boron content in steel is at least 0.0003%. However, boron content in steel exceeding 0.0050% deteriorates formability of a resulting steel sheet. Accordingly, when the steel sheet composition includes boron, boron content in steel is to be B: 0.0003% to 0.0050% (inclusive of 0.0003% and 0.0050%).
  • At least one type of elements selected from Ni: 0.05% to 2.0% (inclusive of 0.05% and 2.0%), and Cu: 0.05% to 2.0% (inclusive of 0.05% and 2.0%)
  • Nickel and copper are elements which each effectively increase strength of steel. These good effects of Ni and Cu are obtained when contents thereof in steel are at least 0.05%, respectively. In a case where at least one of Ni content and Cu content in steel exceeds 2.0%, formability of a resulting steel sheet deteriorates. Accordingly, in a case where the steel sheet composition includes Ni and Cu, contents thereof are to be Ni: 0.05% to 2.0% (inclusive of 0.05% and 2.0%), and Cu: 0.05% to 2.0% (inclusive of 0.05% and 2.0%), respectively.
  • Calcium and REM are useful elements in terms of making sulfides spherical to lessen adverse effects of the sulfides on a steel sheet. Calcium and REM can each cause this effect when contents thereof in steel are at least 0.001%, respectively. In a case where at least one of Ca content and REM content in steel exceeds 0.005%, inclusions increase to cause surface defects, internal defects and the like of a resulting steel sheet.
  • the steel sheet composition includes Ca and REM
  • contents thereof are to be Ca: 0.001% to 0.005% (inclusive of 0.001% and 0.005%) and REM: 0.001% to 0.005% (inclusive of 0.001% and 0.005%), respectively.
  • Components other than those described above are Fe and incidental impurities in the steel sheet of the present invention.
  • the present invention does not exclude a possibility that the steel composition thereof includes a component other than those described above unless inclusion of the component adversely affects the effect of the present invention.
  • a steel material is prepared to have the preferred component composition described above and the steel material is subjected to hot rolling and optionally cold rolling to be finished to a steel sheet material.
  • the processes for hot rolling and cold rolling of a steel material are not particularly restricted in the present invention and may be carried out according to the conventional methods.
  • Examples of typical manufacturing conditions of a steel sheet material include: heating a steel material to temperature in the range of 1000°C to 1300°C (inclusive of 1000°C and 1300C), finishing hot rolling at temperature in the range of 870°C to 950°C (inclusive of 870°C and 950°C); and then subjecting the steel sheet material to coiling at temperature in the range of 350°C to 720°C (inclusive of 350°C and 720°C) to obtain a hot rolled steel sheet.
  • the hot rolled steel sheet thus obtained may further be subjected to pickling and cold rolling at rolling reduction rate in the range of 40% to 90% (inclusive of 40% and 90%) to obtain a cold rolled steel sheet.
  • a steel sheet material of the present invention is manufactured to skip at least a part of the hot rolling process by employing thin slab casting, strip casting or the like.
  • the steel sheet material thus obtained is processed in the following processes to be finished to a high strength press-formed member.
  • the steel sheet material is subjected to heating process.
  • the steel sheet material is to be heated to temperature in the range of 750°C to 1000°C (inclusive of 750°C and 1000°C) and retained in that state for 5 seconds to 1000 seconds (inclusive of 5 seconds and 1000 seconds) in order to suppress coarsening of crystal grains and deterioration of productivity.
  • Heating temperature lower than 750°C may result in insufficient dissolution of carbides in the steel sheet material and possible failure in obtaining the targeted properties of the steel sheet material.
  • the heating temperature exceeding 1000°C causes austenite grains to grow excessively, thereby coarsening the structural phases generated by cooling thereafter to deteriorate toughness and the like of the steel sheet material. Accordingly, the heating temperature is to be in the range of 750°C to 1000°C (inclusive of 750°C and 1000°C).
  • Retention time during which the steel sheet material is retained at the aforementioned temperature is to be in the range of 5 seconds to 1000 seconds (inclusive of 5 seconds and 1000 seconds).
  • the retention time is shorter than 5 seconds, reverse transformation to austenite may not proceed sufficiently and/or carbides in the steel sheet material may not be dissolved sufficiently.
  • the retention time exceeds 1000 seconds, the production cost increases due to too much energy consumption. Accordingly, the retention time is to be in the range of 5 seconds to 1000 seconds (inclusive of 5 seconds and 1000 seconds) and preferably in the range of 60 seconds to 500 seconds (inclusive of 60 seconds and 500 seconds).
  • a temperature range within which hot press-forming is carried out needs to be in the range of 350°C to 900°C (inclusive of 350°C and 900°C) in the present invention.
  • hot press-forming at temperature lower than 350°C, martensitic transformation may partially proceed and the formability-improving effect by hot press-forming may not be attained in a satisfactory manner.
  • a mold may be significantly damaged during hot press-forming to increase production cost.
  • the steel sheet material is then cooled down to temperature in a first temperature region in the range of 50°C to 350°C (inclusive of 50°C and 350°C) so that a portion of martensite proceeds to martensitic transformation.
  • the steel sheet material thus cooled is heated to the austempering temperature in the range of 350°C to 490°C (inclusive of 350°C and 490°C), i.e. a second temperature region as the bainitic transformation temperature region, and retained at the temperature for a period ranging from 5 seconds to 1000 seconds (inclusive of 5 seconds and 1000 seconds) to reliably obtain retained austenite in a stable state.
  • Increase in temperature, from the first temperature region after the cooling up to the second temperature is preferably carried out within 3600 seconds.
  • the first temperature region when the steel sheet material is cooled to temperature below 50°C, most of non-transformed austenite proceeds to martensitic transformation at this stage and sufficient content of bainite (bainitic ferrite and retained austenite) cannot be reliably obtained.
  • the steel sheet material fails to be cooled to temperature equal to or lower than 350°C, tempered martensite cannot be reliably obtained by adequate content. Accordingly, the first temperature region is to be in the range of 50°C to 350°C (inclusive of 50°C and 350°C).
  • Martensite formed by the cooling process from the annealing temperature down to the first temperature region is tempered and non-transformed austenite is transformed into bainite at tempering temperature in the second temperature region.
  • bainite is mainly constituted of lower bainite and the average carbon concentration in austenite may be insufficient.
  • the tempering temperature exceeds 490°C carbides may be precipitated from non-transformed austenite and desired microstructure may not be obtained.
  • the second temperature region is to be in the range of 350°C to 490°C (inclusive of 350°C and 490°C) and preferably in the range of 370°C to 460°C (inclusive of 370°C and 460°C).
  • the retention time at temperature in the second temperature region is to be in the range of 5 seconds to 1000 seconds (inclusive of 5 seconds and 1000 seconds), preferably 15 seconds to 600 seconds (inclusive of 15 seconds and 600 seconds), and more preferably 40 seconds to 400 seconds (inclusive of 40 seconds and 400 seconds).
  • the retention temperature in the series of thermal treatments in the present invention need not be constant and may vary within such predetermined temperature ranges as described above. In other words, variation in each retention temperature within the predetermined temperature range does not adversely affect the spirit of the present invention. Similar tolerance is applied to the cooling rate. Further, the steel sheet of the present invention may be subjected to the relevant thermal treatments in any facilities as long as the required thermal history is satisfied.
  • a steel material obtained from steel having a component composition as shown in Table 1 by using ingot techniques, was heated to 1200°C and subjected to finish hot rolling at 870°C to obtain a hot rolled steel sheet.
  • the hot rolled steel sheet was subjected to coiling at 650°C, pickling, and cold rolling at rolling reduction rate of 65% to obtain a cold rolled steel sheet sample having sheet thickness: 1.2 mm.
  • each of the cold rolled steel sheet samples thus obtained was subjected to heating, retention, hot press-forming, cooling and thermal treatment under the conditions shown in Table 2, whereby a hat-shaped high strength press-formed member sample was prepared.
  • a mold having punch width: 70mm, punch nose radius: 4mm, die shoulder radius: 4mm, and forming depth: 30mm was used.
  • the cold rolled steel sheet sample was heated in ambient air by using either an infrared heating furnace or an atmosphere furnace.
  • the cooling process was then carried out by combining: interposing the steel sheet sample between the punch and the die; and leaving the steel sheet, released from the interposed state, on the die for air-cooling.
  • the heating for tempering and retention, after the cooling process was carried out by using a salt bath furnace.
  • Example 18 O 900 120 730 250 400 90 Example 19 P 850 350 760 200 350 80
  • Example 20 Q 910 180 450 240 410 120
  • Example 21 R 910 180 750 240 400 100
  • Example 22 S 890 200 680 200 400
  • Example 23 T 880 200 750 240 400
  • Example 24 U 880 250 800 250 380
  • Example 25 V 900 180 650 140 400 90
  • Example 26 W 880 200 760 200 400 350
  • Example 20 Q 910 180 450 240 410 120
  • Example 21 R 910 180 750 240 400 100
  • Example 22 S 890 200 680 200 400 90
  • Example 23 T 880 200 750 240 400
  • Example 24 U 880 250 800 250 380
  • Example 25 V 900 180 650 140 400 90
  • Example 26 W 880 200 760 200 400 350
  • Example 18 O 900 120 730 250 400 90
  • Example 19 P 850 350
  • each of the hat-shaped high strength press-formed member samples thus obtained were evaluated by the following methods.
  • a JIS No. 5 test piece and a test sample for analysis were collected, respectively, from a position at the hat bottom of each hat-shaped high strength press-formed member sample.
  • Microstructures often fields of the test sample for analysis were observed by using a ⁇ 3000 scanning electron microscope (SEM) to measure area ratios of respective phases and identify phase structures of respective crystal grains.
  • Quantity of retained austenite was determined by first grinding/polishing the high strength press-formed member sample in the sheet thickness direction to a (thickness ⁇ 1/4) position and then carrying out X-ray diffraction intensity measurement. Specifically, quantity of retained austenite was determined by using Co-K ⁇ as incident X-ray and carrying out necessary calculations based on ratios of diffraction intensities of the respective faces (200), (220), (311) of austenite with respect to diffraction intensities of the respective faces (200), (211) and (220) of ferrite. The quantity of retained austenite thus determined is shown as the area ratio of retained austenite of each high strength press-formed member sample in Table 3.
  • the average carbon concentration in the retained austenite was determined by: obtaining a relevant lattice constant from the intensity peaks of the respective faces (200), (220), (311) of austenite acquired by X-ray diffraction intensity measurement; and substituting the lattice constant for [a 0 ] in the following formula.
  • C % a 0 - 0.3580 - 0.00095 ⁇ Mn % - 0.0056 ⁇ Al % - 0.022 ⁇ N % / 0.0033
  • a 0 lattice constant (nm) and [X%]: mass % of element "X”.
  • Mass % of element X (other than that of carbon) represents mass % of element X with respect to a steel sheet as a whole. In a case where content of retained austenite is 3% or lower, the result was regarded as "measurement failure" because intensity peaks are too low to accurately measure peak positions in such a case.
  • TS tensile strength
  • T.EL. total elongation
  • Example 6 F 36 55 43 0 9 0 100 78 0.82 1278 22 28116
  • Example 7 G 20 69 50 0 11 0 100 72 0.72 1845 10 18450
  • Example 8 H 18 69 59 6 7 0 94 86 0.80 1752 12 21024
  • Example 9 I 21 70 49 0 9 0 100 70 0.83 1599 15 23985
  • Example 10 J 68 15 10 6 11 0 94 67 0.97 1345 17 22865
  • Example 11 K 43 50 30 5 2 0 95 60 - 1310 10 13100 Comp.
  • Example 12 L 37 43 26 10 3 7 83 60 - 1035 13 13455 Comp.
  • Example 18 O 73 12 9 5 10 0 95 75 1.08 1401 15 21015
  • Example 19 P 40 50 22 0 10 0 100 44 0.78 1612 16 25792
  • Example 20 Q 42 44 30 0 14 0 100 68 0.92 1546 15 23190
  • Example 22 S 21 68 49 0 11 0 100 72 0.92 1486 14 20804
  • Example 24 U 62 21 15 4 13 0 96 71 1.18 1412 21 29652
  • Example 25 54 29 20 2 15 0 98 69 0.96 1633 16 26128
  • Example 26 W 32 53 37 0 15 0 100 70 0.89 1735 14 24290
  • Example 27 X 12 82 68 0 6 0 100 83 1.02 1912 11 21032
  • Example ⁇ b Bainitic ferrite in bainite M: Martensite
  • the high strength press-formed member samples according to the present invention unanimously satisfied tensile strength of at least 980 MPa and TS ⁇ T. EL. ⁇ 17000 (MPa ⁇ %). That is, it was confirmed that these member samples according to the present invention unanimously have sufficiently high strength and excellent ductility in a compatible manner.
  • a high strength press-formed member being excellent in ductility and having tensile strength (TS) of at least 980 MPa by setting carbon content in a steel sheet to be at least 0.12% and specifying area ratios of martensite, retained austenite and bainite containing bainitic ferrite with respect to the entire microstructure of the steel sheet and the average carbon concentration in the retained austenite, respectively.
  • TS tensile strength

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
EP11752999.0A 2010-03-09 2011-02-28 High-strength pressed member and method for producing same Active EP2546375B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2010052366A JP5327106B2 (ja) 2010-03-09 2010-03-09 プレス部材およびその製造方法
PCT/JP2011/001164 WO2011111333A1 (ja) 2010-03-09 2011-02-28 高強度プレス部材およびその製造方法

Publications (3)

Publication Number Publication Date
EP2546375A1 EP2546375A1 (en) 2013-01-16
EP2546375A4 EP2546375A4 (en) 2014-06-25
EP2546375B1 true EP2546375B1 (en) 2015-09-30

Family

ID=44563169

Family Applications (1)

Application Number Title Priority Date Filing Date
EP11752999.0A Active EP2546375B1 (en) 2010-03-09 2011-02-28 High-strength pressed member and method for producing same

Country Status (6)

Country Link
US (2) US8992697B2 (uk)
EP (1) EP2546375B1 (uk)
JP (1) JP5327106B2 (uk)
KR (1) KR101420035B1 (uk)
CN (1) CN102906291B (uk)
WO (1) WO2011111333A1 (uk)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102019215053A1 (de) * 2019-09-30 2021-04-01 Thyssenkrupp Steel Europe Ag Verfahren zur Herstellung eines zumindest teilweise vergüteten Stahlblechbauteils und zumindest teilweise vergütetes Stahlblechbauteil

Families Citing this family (87)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5729829B2 (ja) * 2010-11-15 2015-06-03 株式会社神戸製鋼所 温間での延性と深絞り性に優れる温間成形用高強度鋼板およびその製造方法
KR101253885B1 (ko) * 2010-12-27 2013-04-16 주식회사 포스코 연성이 우수한 성형 부재용 강판, 성형 부재 및 그 제조방법
JP5978533B2 (ja) * 2011-03-18 2016-08-24 有限会社リナシメタリ 金属加工方法
JP5736929B2 (ja) * 2011-04-19 2015-06-17 Ｊｆｅスチール株式会社 加工性および低温靭性に優れた中空部材用超高強度電縫鋼管およびその製造方法
CN103547694B (zh) * 2011-04-28 2017-07-25 株式会社神户制钢所 热压成形品及其制造方法
JP5883351B2 (ja) * 2011-06-10 2016-03-15 株式会社神戸製鋼所 熱間プレス成形品、その製造方法および熱間プレス成形用薄鋼板
SE1100523A1 (sv) * 2011-07-06 2013-01-02 Gestamp Hardtech Ab Sätt att varmforma och härda ett tunnplåtsämne
CN103687973B (zh) * 2011-07-15 2016-08-31 Posco公司 热压成形钢板、使用其的成型部件以及制造该钢板和部件的方法
ES2641584T3 (es) 2011-07-21 2017-11-10 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Método para producir un elemento de acero moldeado por presión en caliente
CN103857819B (zh) * 2011-10-04 2016-01-13 杰富意钢铁株式会社 高强度钢板及其制造方法
JP5860308B2 (ja) * 2012-02-29 2016-02-16 株式会社神戸製鋼所 温間成形性に優れた高強度鋼板およびその製造方法
CA2865910C (en) * 2012-03-07 2017-10-17 Nippon Steel & Sumitomo Metal Corporation Steel sheet for hot stamping, method for production thereof, and hot stamping steel material
JP5348268B2 (ja) * 2012-03-07 2013-11-20 Ｊｆｅスチール株式会社 成形性に優れる高強度冷延鋼板およびその製造方法
JP5869924B2 (ja) * 2012-03-09 2016-02-24 株式会社神戸製鋼所 プレス成形品の製造方法およびプレス成形品
JP5802155B2 (ja) * 2012-03-09 2015-10-28 株式会社神戸製鋼所 プレス成形品の製造方法およびプレス成形品
JP5890710B2 (ja) 2012-03-15 2016-03-22 株式会社神戸製鋼所 熱間プレス成形品およびその製造方法
JP5890711B2 (ja) * 2012-03-15 2016-03-22 株式会社神戸製鋼所 熱間プレス成形品およびその製造方法
JP5364859B1 (ja) * 2012-05-31 2013-12-11 株式会社神戸製鋼所 コイリング性と耐水素脆性に優れた高強度ばね用鋼線およびその製造方法
EP2690184B1 (de) * 2012-07-27 2020-09-02 ThyssenKrupp Steel Europe AG Kaltgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung
WO2014020640A1 (ja) * 2012-07-31 2014-02-06 Ｊｆｅスチール株式会社 成形性及び形状凍結性に優れた高強度溶融亜鉛めっき鋼板、並びにその製造方法
CN103805840B (zh) * 2012-11-15 2016-12-21 宝山钢铁股份有限公司 一种高成形性热镀锌超高强度钢板及其制造方法
CN103805838B (zh) 2012-11-15 2017-02-08 宝山钢铁股份有限公司 一种高成形性超高强度冷轧钢板及其制造方法
JP5595609B2 (ja) * 2013-01-18 2014-09-24 株式会社神戸製鋼所 高強度かつ強度−延性バランスに優れた熱間プレス成形鋼部材の製造方法
JP6073154B2 (ja) * 2013-02-21 2017-02-01 株式会社神戸製鋼所 熱間プレス成形品の製造方法
US20140283960A1 (en) * 2013-03-22 2014-09-25 Caterpillar Inc. Air-hardenable bainitic steel with enhanced material characteristics
DE102013009232A1 (de) 2013-05-28 2014-12-04 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Bauteils durch Warmumformen eines Vorproduktes aus Stahl
EP2840159B8 (de) 2013-08-22 2017-07-19 ThyssenKrupp Steel Europe AG Verfahren zum Herstellen eines Stahlbauteils
KR101753016B1 (ko) 2013-09-18 2017-07-03 신닛테츠스미킨 카부시키카이샤 핫 스탬프 성형체 및 그 제조 방법
EP4252930A3 (en) * 2013-10-21 2023-12-20 Magna International Inc Method for trimming a hot formed part
KR20180001590A (ko) * 2013-11-29 2018-01-04 신닛테츠스미킨 카부시키카이샤 열간 성형용 강판
ES2745428T3 (es) 2014-01-06 2020-03-02 Nippon Steel Corp Acero y método para fabricar el mismo
EP3093359A4 (en) 2014-01-06 2017-08-23 Nippon Steel & Sumitomo Metal Corporation Hot-formed member and process for manufacturing same
MX2016008473A (es) * 2014-01-30 2016-10-12 Nippon Steel & Sumitomo Metal Corp Metodo de calentamiento de lamina de acero y aparato de calentamiento de lamina de acero.
WO2015152263A1 (ja) * 2014-03-31 2015-10-08 新日鐵住金株式会社 ホットスタンプ鋼材
RU2659532C2 (ru) * 2014-03-31 2018-07-02 Ниппон Стил Энд Сумитомо Метал Корпорейшн Горячештампованная сталь
JP5825413B1 (ja) * 2014-04-23 2015-12-02 Ｊｆｅスチール株式会社 熱間プレス成形品の製造方法
WO2016001703A1 (en) 2014-07-03 2016-01-07 Arcelormittal Method for manufacturing a high strength steel sheet and sheet obtained by the method
WO2016001705A1 (en) * 2014-07-03 2016-01-07 Arcelormittal Method for manufacturing a high strength steel sheet having improved formability and ductility and sheet obtained
WO2016001699A1 (en) * 2014-07-03 2016-01-07 Arcelormittal Method for manufacturing a high strength steel sheet having improved formability and sheet obtained
JP5861749B1 (ja) * 2014-07-30 2016-02-16 Ｊｆｅスチール株式会社 プレス成形方法
CN104195455B (zh) * 2014-08-19 2016-03-02 中国科学院金属研究所 一种基于碳配分原理的热冲压烘烤韧化钢及其加工方法
CN104213040B (zh) * 2014-08-27 2016-02-17 南京创贝高速传动机械有限公司 一种高强度轴承的专用钢材及其加工工艺
CN106661698B (zh) * 2014-08-28 2018-09-04 杰富意钢铁株式会社 延伸凸缘性、延伸凸缘性的面内稳定性及弯曲性优异的高强度熔融镀锌钢板以及其制造方法
KR101931041B1 (ko) * 2014-10-24 2018-12-19 제이에프이 스틸 가부시키가이샤 고강도 핫 프레스 부재 및 그 제조 방법
WO2016079565A1 (en) 2014-11-18 2016-05-26 Arcelormittal Method for manufacturing a high strength steel product and steel product thereby obtained
US20160145731A1 (en) * 2014-11-26 2016-05-26 GM Global Technology Operations LLC Controlling Liquid Metal Embrittlement In Galvanized Press-Hardened Components
WO2016106621A1 (en) * 2014-12-31 2016-07-07 GM Global Technology Operations LLC Method of hot forming a component from steel
WO2016151345A1 (fr) * 2015-03-23 2016-09-29 Arcelormittal Pieces a structure bainitique a hautes proprietes de resistance et procede de fabrication
WO2016157863A1 (ja) * 2015-03-31 2016-10-06 Ｊｆｅスチール株式会社 高強度・高靭性鋼板およびその製造方法
RU2606665C1 (ru) * 2015-07-06 2017-01-10 Общество с ограниченной ответственностью "Алтайский сталелитейный завод" Способ регулируемой термической обработки литых стальных деталей
RU2718651C2 (ru) * 2015-12-18 2020-04-13 Аутотек Инжиниринг, С.Л. Центральная балка центральной стойки кузова и способ ее изготовления
KR101696121B1 (ko) 2015-12-23 2017-01-13 주식회사 포스코 내수소지연파괴특성, 내박리성 및 용접성이 우수한 열간성형용 알루미늄-철 합금 도금강판 및 이를 이용한 열간성형 부재
MX2018009735A (es) 2016-02-10 2019-01-24 Jfe Steel Corp Lamina de acero de alta resistencia y metodo para fabricar la misma.
DE102016104800A1 (de) 2016-03-15 2017-09-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines warmumgeformten Stahlbauteils und ein warmumgeformtes Stahlbauteil
JP6508176B2 (ja) * 2016-03-29 2019-05-08 Ｊｆｅスチール株式会社 ホットプレス部材およびその製造方法
US10619223B2 (en) 2016-04-28 2020-04-14 GM Global Technology Operations LLC Zinc-coated hot formed steel component with tailored property
US10385415B2 (en) 2016-04-28 2019-08-20 GM Global Technology Operations LLC Zinc-coated hot formed high strength steel part with through-thickness gradient microstructure
US10288159B2 (en) 2016-05-13 2019-05-14 GM Global Technology Operations LLC Integrated clutch systems for torque converters of vehicle powertrains
CN106399837B (zh) 2016-07-08 2018-03-13 东北大学 热冲压成形用钢材、热冲压成形工艺及热冲压成形构件
US10240224B2 (en) 2016-08-12 2019-03-26 GM Global Technology Operations LLC Steel alloy with tailored hardenability
WO2018033960A1 (ja) * 2016-08-16 2018-02-22 新日鐵住金株式会社 熱間プレス成形部材
CN109642281B (zh) 2016-08-31 2021-02-23 杰富意钢铁株式会社 高强度冷轧薄钢板及其制造方法
JP6424195B2 (ja) 2016-11-14 2018-11-14 株式会社豊田中央研究所 熱間プレス成形方法
JP6460296B2 (ja) 2016-11-25 2019-01-30 新日鐵住金株式会社 焼き入れ成形品の製造方法、熱間プレス用鋼材の製造方法、及び熱間プレス用鋼材
CA3067159A1 (en) * 2016-11-29 2018-06-07 Tata Steel Ijmuiden B.V. Method for manufacturing a hot-formed article, and obtained article
KR101917447B1 (ko) 2016-12-20 2018-11-09 주식회사 포스코 고온연신 특성이 우수한 고강도 강판, 온간프레스 성형부재 및 이들의 제조방법
US10260121B2 (en) 2017-02-07 2019-04-16 GM Global Technology Operations LLC Increasing steel impact toughness
WO2019092481A1 (en) * 2017-11-10 2019-05-16 Arcelormittal Cold rolled steel sheet and a method of manufacturing thereof
US20210087661A1 (en) * 2017-12-28 2021-03-25 GM Global Technology Operations LLC Steel for hot stamping with enhanced oxidation resistance
JP6460287B1 (ja) * 2018-03-29 2019-01-30 新日鐵住金株式会社 ホットスタンプ用鋼板
WO2019208556A1 (ja) 2018-04-23 2019-10-31 日本製鉄株式会社 鋼部材およびその製造方法
CN108374127A (zh) 2018-04-28 2018-08-07 育材堂（苏州）材料科技有限公司 热冲压成形用钢材、热冲压成形工艺及热冲压成形构件
CN112513310A (zh) 2018-05-24 2021-03-16 通用汽车环球科技运作有限责任公司 改善压制硬化钢的强度和延性的方法
CN112534078A (zh) 2018-06-19 2021-03-19 通用汽车环球科技运作有限责任公司 具有增强的机械性质的低密度压制硬化钢
CN112313352B (zh) * 2018-06-29 2023-06-27 东洋钢钣株式会社 热轧钢板、高强度冷轧钢板及它们的制造方法
CN111197145B (zh) 2018-11-16 2021-12-28 通用汽车环球科技运作有限责任公司 钢合金工件和用于制造压制硬化钢合金部件的方法
KR102276740B1 (ko) * 2018-12-18 2021-07-13 주식회사 포스코 연성 및 가공성이 우수한 고강도 강판 및 그 제조방법
US11795520B2 (en) * 2019-02-22 2023-10-24 Jfe Steel Corporation Hot-pressed member, method for manufacturing the same, and method for manufacturing steel sheet for hot-pressed member
CN113557316B (zh) * 2019-04-01 2022-10-04 日本制铁株式会社 热冲压成形品和热冲压用钢板、以及它们的制造方法
WO2020221889A1 (en) * 2019-04-30 2020-11-05 Tata Steel Nederland Technology B.V. A high strength steel product and a process to produce a high strength steel product
US11530469B2 (en) 2019-07-02 2022-12-20 GM Global Technology Operations LLC Press hardened steel with surface layered homogenous oxide after hot forming
US20210189516A1 (en) * 2019-12-20 2021-06-24 Benteler Steel/Tube Gmbh Tube product, hollow carrier of perforating gun and method of manufacturing the tube product
CN113025876A (zh) 2019-12-24 2021-06-25 通用汽车环球科技运作有限责任公司 高性能压制硬化钢组件
US20230002874A1 (en) * 2020-01-09 2023-01-05 Nippon Steel Corporation Hot-stamping formed body
JP7319569B2 (ja) * 2020-01-09 2023-08-02 日本製鉄株式会社 ホットスタンプ成形体
MX2022008472A (es) * 2020-01-16 2022-08-02 Nippon Steel Corp Carroceria estampada en caliente.
CN115362280B (zh) * 2020-04-03 2023-10-17 日本制铁株式会社 钢板及其制造方法

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007034063A1 (fr) 2005-09-21 2007-03-29 Arcelormittal France Procede de fabrication d’une piece en acier de microstructure multi-phasee
WO2009099079A1 (ja) 2008-02-08 2009-08-13 Jfe Steel Corporation 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE435527B (sv) 1973-11-06 1984-10-01 Plannja Ab Forfarande for framstellning av en detalj av herdat stal
GB1490545A (en) 1974-12-20 1977-11-02 Blanco A Solar heating
JP4412727B2 (ja) 2004-01-09 2010-02-10 株式会社神戸製鋼所 耐水素脆化特性に優れた超高強度鋼板及びその製造方法
JP4673558B2 (ja) * 2004-01-26 2011-04-20 新日本製鐵株式会社 生産性に優れた熱間プレス成形方法及び自動車用部材
JP4445365B2 (ja) * 2004-10-06 2010-04-07 新日本製鐵株式会社 伸びと穴拡げ性に優れた高強度薄鋼板の製造方法
JP4735211B2 (ja) * 2004-11-30 2011-07-27 Ｊｆｅスチール株式会社 自動車用部材およびその製造方法
EP1676932B1 (en) * 2004-12-28 2015-10-21 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) High strength thin steel sheet having high hydrogen embrittlement resisting property
JP2006183189A (ja) * 2004-12-28 2006-07-13 Knit Glove Kk 履き口部分にスリットを有する靴下
JP2007016296A (ja) 2005-07-11 2007-01-25 Nippon Steel Corp 成形後の延性に優れたプレス成形用鋼板及びその成形方法、並びにプレス整形用鋼板を用いた自動車用部材
CN101460647B (zh) * 2006-07-14 2015-05-20 株式会社神户制钢所 高强度钢板及其制造方法
JP5151246B2 (ja) 2007-05-24 2013-02-27 Ｊｆｅスチール株式会社 深絞り性と強度−延性バランスに優れた高強度冷延鋼板および高強度溶融亜鉛めっき鋼板ならびにその製造方法
JP5418047B2 (ja) * 2008-09-10 2014-02-19 Ｊｆｅスチール株式会社 高強度鋼板およびその製造方法
JP5412182B2 (ja) * 2009-05-29 2014-02-12 株式会社神戸製鋼所 耐水素脆化特性に優れた高強度鋼板

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007034063A1 (fr) 2005-09-21 2007-03-29 Arcelormittal France Procede de fabrication d’une piece en acier de microstructure multi-phasee
WO2009099079A1 (ja) 2008-02-08 2009-08-13 Jfe Steel Corporation 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
EP2267176A1 (en) 2008-02-08 2010-12-29 JFE Steel Corporation High-strength hot-dip galvanized steel sheet with excellent processability and process for producing the same

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
K. MORI ET AL.: "Warm and Hot Stamping of Ultra High Tensile Strength Steel Sheets Using Resistance Heating", CIRP ANNALS, MANUFACTURING TECHNOLOGY, vol. 54, no. Issue 1, 2005, pages 209 - 212, XP027601570
T. ALTAN: "Hot-stamping boron-alloyed steels for automotive parts - Part I: Process methods and uses", STAMPING JOURNAL, December 2006 (2006-12-01), pages 40 - 41, XP009179671

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102019215053A1 (de) * 2019-09-30 2021-04-01 Thyssenkrupp Steel Europe Ag Verfahren zur Herstellung eines zumindest teilweise vergüteten Stahlblechbauteils und zumindest teilweise vergütetes Stahlblechbauteil
WO2021063747A1 (de) 2019-09-30 2021-04-08 Thyssenkrupp Steel Europe Ag Verfahren zur herstellung eines zumindest teilweise vergüteten stahlblechbauteils und zumindest teilweise vergütetes stahlblechbauteil

Also Published As

Publication number Publication date
US8992697B2 (en) 2015-03-31
WO2011111333A1 (ja) 2011-09-15
EP2546375A1 (en) 2013-01-16
CN102906291A (zh) 2013-01-30
EP2546375A4 (en) 2014-06-25
US20130048161A1 (en) 2013-02-28
US20140096876A1 (en) 2014-04-10
KR20120121406A (ko) 2012-11-05
JP5327106B2 (ja) 2013-10-30
CN102906291B (zh) 2014-12-17
JP2011184758A (ja) 2011-09-22
US9644247B2 (en) 2017-05-09
KR101420035B1 (ko) 2014-07-16

Similar Documents

Publication Publication Date Title
EP2546375B1 (en) High-strength pressed member and method for producing same
EP3415656B1 (en) High-strength steel sheet and method for manufacturing same
EP3020845B1 (en) Hot-stamp part and method of manufacturing the same
TWI412609B (zh) 高強度鋼板及其製造方法
EP3214199B1 (en) High-strength steel sheet, high-strength hot-dip galvanized steel sheet, high-strength hot-dip aluminum-coated steel sheet, and high-strength electrogalvanized steel sheet, and methods for manufacturing same
EP2824210B1 (en) High-strength cold-rolled steel sheet and process for manufacturing same
EP2559783B1 (en) High-strength hot-rolled steel plate exhibiting excellent stretch flangeability and fatigue resistance properties, and production method therefor
EP2546382B1 (en) High-strength steel sheet and method for producing same
US8876987B2 (en) High-strength steel sheet and method for manufacturing same
TWI412605B (zh) 高強度鋼板及其製造方法
EP1870483B1 (en) Hot-rolled steel sheet, method for production thereof and workedd article formed therefrom
EP2942414B1 (en) Thick, tough, high tensile strength steel plate and production method therefor
EP3214193A1 (en) High-strength steel sheet, high-strength hot-dip galvanized steel sheet, high-strength hot-dip aluminum-coated steel sheet, and high-strength electrogalvanized steel sheet, and methods for manufacturing same
EP2546368A1 (en) Method for producing high-strength steel sheet
EP3543364B1 (en) High-strength steel sheet and method for producing same
EP2695961B1 (en) High-strength steel sheet excellent in workability and manufacturing method thereof
EP3719148A1 (en) High-hardness steel product and method of manufacturing the same
EP2792762A1 (en) High-yield-ratio high-strength cold-rolled steel sheet and method for producing same
EP2578714B1 (en) Hot-rolled high-strength steel sheet and process for production thereof
EP3543365B1 (en) High-strength steel sheet and method for producing same
EP3730651A1 (en) High yield ratio-type high-strength steel sheet and method for manufacturing same
EP4079906A1 (en) Structural steel material and method for manufacturing same

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20120906

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20140528

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/06 20060101ALI20140522BHEP

Ipc: C21D 9/00 20060101ALI20140522BHEP

Ipc: C21D 1/22 20060101ALI20140522BHEP

Ipc: C22C 38/00 20060101AFI20140522BHEP

Ipc: C21D 8/02 20060101ALI20140522BHEP

Ipc: C22C 38/02 20060101ALI20140522BHEP

Ipc: C22C 38/04 20060101ALI20140522BHEP

Ipc: C21D 1/18 20060101ALI20140522BHEP

Ipc: C22C 38/60 20060101ALI20140522BHEP

Ipc: C21D 9/46 20060101ALI20140522BHEP

Ipc: B21D 22/20 20060101ALI20140522BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20150512

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 752467

Country of ref document: AT

Kind code of ref document: T

Effective date: 20151015

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602011020174

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20151230

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20151231

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20150930

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 752467

Country of ref document: AT

Kind code of ref document: T

Effective date: 20150930

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 6

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160130

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160229

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160201

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

REG Reference to a national code

Ref country code: DE

Ref legal event code: R026

Ref document number: 602011020174

Country of ref document: DE

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

26 Opposition filed

Opponent name: ARCELORMITTAL

Effective date: 20160628

PLAX Notice of opposition and request to file observation + time limit sent

Free format text: ORIGINAL CODE: EPIDOSNOBS2

R26 Opposition filed (corrected)

Opponent name: ARCELORMITTAL

Effective date: 20160628

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: LU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160228

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160229

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160229

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

PLBB Reply of patent proprietor to notice(s) of opposition received

Free format text: ORIGINAL CODE: EPIDOSNOBS3

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PLAB Opposition data, opponent's data or that of the opponent's representative modified

Free format text: ORIGINAL CODE: 0009299OPPO

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 7

R26 Opposition filed (corrected)

Opponent name: ARCELORMITTAL

Effective date: 20160628

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160228

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 8

PLCK Communication despatched that opposition was rejected

Free format text: ORIGINAL CODE: EPIDOSNREJ1

APBM Appeal reference recorded

Free format text: ORIGINAL CODE: EPIDOSNREFNO

APBP Date of receipt of notice of appeal recorded

Free format text: ORIGINAL CODE: EPIDOSNNOA2O

APAH Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOSCREFNO

APBQ Date of receipt of statement of grounds of appeal recorded

Free format text: ORIGINAL CODE: EPIDOSNNOA3O

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20110228

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160229

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

APAH Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOSCREFNO

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150930

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20200219

Year of fee payment: 10

APBU Appeal procedure closed

Free format text: ORIGINAL CODE: EPIDOSNNOA9O

REG Reference to a national code

Ref country code: DE

Ref legal event code: R100

Ref document number: 602011020174

Country of ref document: DE

PLBN Opposition rejected

Free format text: ORIGINAL CODE: 0009273

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: OPPOSITION REJECTED

27O Opposition rejected

Effective date: 20200723

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20210228

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210228

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230512

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20231229

Year of fee payment: 14

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20240103

Year of fee payment: 14